CN105648263B - A kind of high strength easy processing Cu-base composites and preparation method thereof - Google Patents
A kind of high strength easy processing Cu-base composites and preparation method thereof Download PDFInfo
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- CN105648263B CN105648263B CN201610009639.5A CN201610009639A CN105648263B CN 105648263 B CN105648263 B CN 105648263B CN 201610009639 A CN201610009639 A CN 201610009639A CN 105648263 B CN105648263 B CN 105648263B
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C9/00—Alloys based on copper
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- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
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Abstract
A kind of high strength easy processing Cu-base composites and preparation method thereof.The composite material is changed using phase structure conversion characteristic specific to the Fe C phases in alloy substrate, i.e. face-centered cubic to martensite or body-centered cubic, the intensity and processing performance of Effective Regulation composite material.Tiny Fe C phases particle contained by material can not only even dispersion be distributed in material matrix, and with face-centred cubic structure so that composite material exhibits go out excellent processing performance, σ0.2=171.5MPa, σb=361.6MPa, δ=35%.And pass through follow-up ultralow temperature cold rolling deformation process so that the composite material strength is increased substantially, σ0.2=519.6MPa, σb=568.1MPa, δ=5%, this deep cooling, which rolls state material, to advanced optimize regulation and control to its processing performance and intensity by subsequent Low Temperature Heat Treatment.The processing performance and intensity of the material are significantly better than that the Cu-base composites that ceramic particle is strengthened, and production cost is relatively low, can not only be in the extensive use of numerous high-technology fields, and can also be widely used in many civilian industries.
Description
Technical field
The invention belongs to Cu-base composites technical field, be related to it is a kind of can industrial applications high strength easy processing novel
Cu-base composites and preparation method thereof to novel based composites mechanical property and add particular for numerous high-technology fields
The increasingly harsher present situation of work performance requirement and develop.Composite material prepared by the preparation method can ensure it with height
Intensity and excellent processing performance, and its production cost strengthens the production cost of Cu-base composites far below ceramic particle.
Background technology
Copper, copper alloy and Cu-base composites are the earliest metalloid materials of mankind's application.Up to the present, yield
Steel and aluminium are only second to, is widely used in the industrial departments such as machine-building, transport, building, electrical, electronics.In recent years, with
The fast development of the electronics and information industries such as microelectronics, computer, communication, industry automatic control and automobile industry, such material
Using becoming more extensive, demand also increases year by year, and also more and more harsh to its performance requirement.Knot particularly therein
Structure function copper alloy or Cu-base composites, such as high-strength highly-conductive, high strength and medium conductivity and super high-strength copper alloy (or composite material),
It is paid close attention to all the time by people.Although such material largely contains ceramic particle, two are broadly divided into according to size
Class, one kind is that a certain amount of Nano Ceramic Particles (size is less than 100nm) are distributed in matrix, and another kind of be distributed in matrix
A certain amount of micro-ceramic particle., since nano-particles size is smaller, general concentration cannot be too high for the former, is otherwise easy to occur
Particle aggregation and the comprehensive performance for reducing material.The Cu-Al most typically prepared using internal oxidition2O3Dispersion-strengthened Cu closes
Gold, the material comprehensive performance is more excellent, can simultaneously with high strength ＆ high electric-conduction and high temperature resistance softening performance etc.,
But the material is due to production technology complexity so that production cost is higher and then seriously limits its extensive use；Although in addition,
Nano Ceramic Particles even dispersion, which is distributed in alloy substrate, can significantly hinder dislocation line movement, so that alloy strength obtains
It increases substantially, and nano-particle will not crack or generate micro-crack etc. in deformation process, but intensity is increased
Simultaneously but also the corresponding difficulty of processing of such material increases, high temperature process must be utilized to deform in forming process, such as hot extrusion
Deng.(such as 0.23vol%Al when ceramic particle concentration is relatively low2O3) such Alloy At Room Temperature processing performance is relatively preferable, and due to closing
The golden relatively low high temperature hot extrusion process of intensity is relatively easy to realize.Increase however as dispersed granules concentration, the strength of materials substantially rises
Height, one side extruder tonnage sufficiently high must can just carry out crimp, again such that the cost and difficulty of material preparation process
Degree increases；On the other hand since matrix and hardening constituent particle compatibility of deformation difference and the two heat are swollen during its high temperature deformation
Swollen difference of coefficients is larger, it is easy to cracking occur or generate micro-crack in interface, even the low-down Cu- of concentration
0.23vol%Al2O3Alloy is no exception, this problem but also such material the production cost increases.
For containing the Cu-base composites of a certain amount of micrometer ceramics particle in another kind of Copper substrate, due to equally distributed
Ceramic particle not only can be with efficient hardening Copper substrate, but also can mitigate composite density or even some copper-based composite woods
Material using add the second special phase and so that the thermal conductivity of composite material is significantly improved, such as Cu/ diamonds and Cu/SiC
Composite material etc..Therefore, this kind of Cu-base composites also obtained fast-developing in recent years, and preparation method diversification also occurs and becomes
Gesture, but mainly include powder metallurgy and melting or infiltration method etc..Band while such strength of materials acquisition increases substantially
Another outstanding problem come is that difficulty of processing increases or some composite materials more originally can not be processed deformation.There is this
The main reason for problem is since ceramic particle and matrix can not carry out compatible deformation, and be easy in deformation process in particle
Interior generation micro-crack or cracking phenomena, so that such composite processing plasticity is very low.This problem is still at present
Such material is badly in need of one of critical issue solved.
It is strong common to the Cu-base composites strengthened for above-mentioned nano-particle dispersion strengthening copper alloy and ceramic particle
The problem of degree and processing performance cannot be taken into account very well etc., if we can develop a kind of not only mechanical property it is very excellent but also
Processing performance also very excellent novel copper-based composite material, development for Cu-base composites and preferably meets high
New technical field is of great significance to the widespread demand of high-strength highly-conductive easy processing advanced composite material (ACM).
Invention content
The present invention strengthens copper-based compound for overcome the deficiencies in the prior art for various ceramic particles existing at present
The problems such as material generally existing intensity is higher and processing performance is poor, exploitation are a kind of with high intensity and excellent processability
Novel copper-based composite material.The novel copper-based composite material makes full use of Fe and C element solid solubility extremely low in Cu matrixes,
Fe-C phases can occur phase transformation between austenite and martensite and both structures mutually significant performance difference (that is, Fe-C phases
For face-centred cubic structure during in austenite, there is excellent processing performance, and intensity is very high during in martensitic structure can be with
Significant contribution is generated, while austenite can be occurred to martensite transfor mation by strain inducing to Cu matrix strengthenings), so as to fulfill
The fine combination of high intensity and high formability.In addition, if Copper substrate can obtain nanometer crystal microstructure, can not only cause copper-based
Composite material strength is more improved, but also can be effectively increased the plasticity of composite material.The present invention is namely based on
What this thought was designed and developed, it is face-centered cubic Fe-C that simplified summary, which is exactly prepared by melting and casting containing a certain amount of structure,
Then by special machining deformation technique, it is required on the one hand so that composite processing is deformed into for the Cu-base composites of phase
Plank etc.；On the other hand but also martensitic traoformation occurs for Fe-C, so as to efficient hardening Copper substrate, together during machining deformation
When deformation during it is also possible that Copper substrate obtain processing hardening and containing a large amount of dislocation born of the same parents organize；This state it is copper-based compound
Although material has higher-strength, if be heat-treated by follow-up certain temperature, it can not only regulate and control the dislocation of Copper substrate
Born of the same parents' tissue makes it be converted into nanometer crystal microstructure, but also can further make the Fe being dissolved in Copper substrate and C element that timeliness occur
It is precipitated, it is final so that developing Cu-base composites intensity and plasticity obtains and further improve.The invention alloy is suitble to apply
In numerous technical fields, have especially for the processing performance and production cost of copper alloy with high strength and high conductivity or Cu-base composites
The industries such as the production and manufacture of necessarily required numerous high-technology fields and the product for civilian use, while also be adapted for or prepare
Manufacturer's application of the similar copper alloy of production or Cu-base composites product.
The present invention first selects the composition range of novel copper-based composite material by composition design and optimization, then
By composite material designed by the preparation of the processes such as melting and casting and its mechanical property and processing performance are studied, it is final to determine
Novel copper-based composite material compositions range and corresponding preparation method with excellent processability.Specific preparation process is such as
Under：Novel copper-based composite material compositions selection → FeCx master alloys melting and casting → novel copper-based composite material preparation and melting
→ novel copper-based composite material quickly solidifies → and to roll deformation induced martensitic traoformation → heat treatment regulation and control logical for ultralow temperature deep cooling repeatedly
Matrix grain size is mutually precipitated with nanoprecipitation → composite board of excellent combination property.
It is a kind of with high intensity and the novel copper-based composite material of excellent processability, it is characterised in that the composite material
Chemical composition and its mass percentage content be：Fe:9.0~12.0wt%, C：0.05~0.5wt%, P≤0.02wt%,
Si≤0.01wt%, Ni≤0.01wt%, Zn≤0.01wt%, Al≤0.01wt%, B≤0.01wt%, surplus Cu, wherein
C/Fe mass ratioes ranging from 0.01~0.8wt% of chemical composition Fe, C.
Preferably, the Fe of chemical composition and C content range are respectively 9.5~11.5wt% of Fe, and C 0.054~
C/Fe mass ratioes ranging from 0.04~0.7wt% of 0.2wt%, wherein chemical composition Fe, C.
It is above-mentioned with high intensity and the preparation method of the novel copper-based composite material of excellent processability, the preparation side
Method includes the following steps：
Step 1: novel copper-based composite material vacuum melting；
Step 2: novel copper-based composite material quickly solidifies；
Step 3: novel copper-based composite material repeatedly the deformation induced martensitic traoformation process of ultralow temperature (or in deep cooling
Certain high temperature, short time heat treatment is carried out before deformation first, the deformation induced martensitic phase of ultralow temperature is then carried out repeatedly again and exchanges work
Skill processing)；
Step 4: the heat treatment regulation and control of novel copper-based composite material nanometer crystalline substance tissue.
Preferably, the novel copper-based composite material vacuum melting of the step 1 and step 2 and fast solidification technology are specific
For：Raw material are placed in vaccum sensitive stove crucible and then burner hearth is vacuumized first, treat that burner hearth vacuum degree is reduced to 4Pa
Vacuum pump is closed when following, while is filled with high-purity Ar gas and stops inflation when burner hearth vacuum degree reaches more than 0.02MPa, continues to take out
Vacuum keeps the temperature more than 10min when being warming up to 400~500 DEG C first, then proceedes to heat up to starting to heat up step by step during below 4Pa
It is kept the temperature to 1500 DEG C or more, 2~8min is stood after the raw material such as Fe-C intermediate alloys and high-purity Cu thoroughly fusing, it then will be molten
Temperature reduction is to 1220~1380 DEG C and places 2~5min, and alloy melt is then warming up to 1500 DEG C or more again and stands 2
~5min, then reduce electric current reduces melt temperature to 1150~1280 DEG C, and cast in the water cooling of logical recirculated water again
In copper mold, cooling velocity is controlled 1.1 × 102DEG C/s~8.8 × 104DEG C/s in the range of；
Preferably, the novel copper-based composite material of the step 3 deformation induced martensitic traoformation process of ultralow temperature repeatedly
Specially：Sample is placed into more than 30min in liquid nitrogen container first, then carries out ultralow warm deformation, deformation temperature：- 100~-190
DEG C, deflection：20%~29%, mode of texturing：Symmetric rolling, pass deformation are 10~20%；Then again by ultralow warm-rolling
Panel is put into 2~9min of cooling, deformation temperature in liquid nitrogen container：- 100~-190 DEG C, deflection：20%~29%, deformation side
Formula：Symmetric rolling, pass deformation：10~20%；Then again by ultralow temperature rolled plate be put into liquid nitrogen container cooling 2~
5min, deformation temperature：- 100~-190 DEG C, deflection：20%~29%, mode of texturing：Symmetric rolling, pass deformation：10
~20%；Ultralow temperature rolled plate is finally put into 1~3min of cooling, deformation temperature in liquid nitrogen container again：- 100~-190 DEG C, become
Shape amount：15%~25%, mode of texturing：Symmetric rolling, pass deformation：5~15%.
Preferably, the novel copper-based composite material of the step 3 deformation induced martensitic traoformation process of ultralow temperature repeatedly
If be heat-treated using certain high temperature, short time is first carried out, ultralow temperature deformation process repeatedly, high temperature, short time heat are then carried out again
Treatment process is specially：It is carried out in heat-treatment furnace with inert gas shielding, 800~920 DEG C of heat treatment temperature, time 2min
~20min, is then cooled down using water quenching method.
Preferably, the heat treatment regulation and control concrete technology of the novel copper-based composite material nanometer crystalline substance tissue of the step 4 is：Band
Have in the heat-treatment furnace of inert gas shielding and carry out, then 100~400 DEG C of heat treatment temperature, time 5min~120min is used
Water quenching method is cooled down.
By using above-mentioned technical solution, the present invention has following superiority：The novel copper-based composite material of the present invention
The austenite of fcc structure can be induced to Martensite phase transition by making full use of the Fe-C phases in matrix that can be deformed by deep cooling；
And on the other hand can make Copper substrate crystal grain refinement in deep cooling rolls deformation process, it can be obtained through subsequent heat treatment process control
Nanometer crystal microstructure, it is final so that exploitation material is with high intensity so as to further improve the intensity and plasticity of composite material
And excellent processing performance.Material of the present invention and preparation method thereof is highly suitable to be applied for the strength of materials, conductivity, processing
Performance and production cost have certain requirements the processing and production of numerous civilian industry Related products, also are adapted for applying certainly
In the other high-technology fields having higher requirements to high strength composite processing performance.
Description of the drawings
Novel copper-based composite material metallographic microstructure prepared by Fig. 1 comparative examples 1；
Novel copper-based composite material metallographic microstructure prepared by Fig. 2 embodiments 1；
Novel copper-based composite material metallographic microstructure prepared by Fig. 3 comparative examples 2；
Novel copper-based composite material metallographic microstructure prepared by Fig. 4 embodiments 2；
Novel copper-based composite material metallographic microstructure prepared by Fig. 5 embodiments 3.
Specific embodiment
The present invention is further supplemented and described with reference to specific embodiment.
The high-purity Cu of electrolysis, high-purity Fe and high-purity C of 99.9wt% etc. is respectively adopted in raw material.Frequency induction furnace in a vacuum
Middle melting Fe-C intermediate alloys, the wherein scaling loss of Elements C are carried out by 2~6wt%, and vacuum degree is less than 10Pa, and smelting temperature exists
1560~1610 DEG C, 1~3min is stood before casting, cast temperature is at 1500~1540 DEG C, and then direct pouring is in ordinary steel
In mould.It is designed according to novel copper-based composite material compositions, cuts the Fe-C intermediate alloys and height of a certain amount of common punching block casting
The raw material such as pure Cu are placed in corundum crucible and carry out melting using vacuum medium frequency induction furnace.Specific smelting technology is, first
It vacuumizes, vacuum pump is closed, while be filled with Ar gas and treat that burner hearth vacuum degree reaches 0.015MPa when vacuum degree in furnace body is less than 5Pa
More than when stop inflation, continue to be evacuated down to below 5Pa and start to heat up step by step, 8min is kept the temperature when being warming up to 300~600 DEG C first
More than, then proceed to be warming up to 1500 DEG C or more, after the raw material such as Fe-C intermediate alloys and high-purity Cu thoroughly fusing after stand 1~
Then melt temperature is reduced to 1200~1400 DEG C and places 1~5min, is then warming up to alloy melt again by 10min
1500 DEG C or more 1~5min of standing, then reduce electric current reduces melt temperature to 1100~1300 DEG C, and cast in again
In the water cooled copper mould of logical recirculated water, cooling velocity is controlled 1 × 102DEG C/s~9 × 104DEG C/s in the range of.Carry out an invention composite wood
The specific chemical composition of material is shown in Table 1.
Table 1 carries out an invention Cu-base composites chemical composition (mass percent, wt%)
| Element | Fe | C | P | Si | Ni | Zn | Al | B | Cu |
| Content | 10.0 | 0.06 | ≤0.02 | ≤0.01 | ≤0.01 | ≤0.01 | ≤0.01 | ≤0.01 | Surplus |
Invention Cu-base composites ingot casting can induce Fe-C phases in Copper substrate that horse occurs by ultralow temperature depth cold-rolling deformation
Family name's body phase transformation so that novel copper-based composite material strength is obviously improved, finally carries out it being suitably heat-treated and not only may be used
So that generating a large amount of nanometer crystal microstructures in Copper substrate, but also a large amount of nanoscale Fe-C phases can be precipitated so that high formability
Cu-base composites intensity, which obtains, further to be improved.Specifically treatment process is：To quickly solidify state Cu-base composites into
The a certain amount of multiple ultralow temperature deep cooling of row, which rolls deformation process, makes Fe-C phases in matrix that strain inducing martensitic traoformation, strain temperature occur
It it is -100~-190 DEG C, overall strain amount is 60%~95%, and passage dependent variable is 2%~20%；Or it carries out first centainly
High temperature, short time, which is heat-treated, to be initially formed a certain amount of martensite in matrix, then carries out deep cold-rolling deformation again, specific high
Heat treatment process is temperature in short-term：It is carried out in heat-treatment furnace with inert gas shielding, 800~950 DEG C of heat treatment temperature, the time
Then 2min~30min is cooled down using water quenching method.Certain Low Temperature Heat Treatment, heat are finally carried out to deep cooling rolled material
Treatment process is specially：It is carried out in heat-treatment furnace with inert gas shielding, 50~450 DEG C of heat treatment temperature, time 2min
~150min, is then cooled down using water quenching method.Specific embodiment is as follows：
Comparative example 1
According to invention Cu-base composites composition design value, the raw material such as high-purity Cu and Fe-C intermediate alloys are cut first
It is placed in vacuum medium frequency induction furnace, melting and casting is carried out to it, specific melt casting process is：First burner hearth take out true
Sky closes vacuum pump when burner hearth vacuum degree is reduced to below 4Pa, while is filled with high-purity Ar gas and treats that burner hearth vacuum degree reaches
Stop inflation during more than 0.02MPa, start to heat up step by step when continuing to be evacuated down to below 4Pa, be warming up to 400~500 DEG C first
More than Shi Baowen 10min, then proceed to be warming up to 1500 DEG C or more and keep the temperature, and treat that the raw material such as Fe-C intermediate alloys and high-purity Cu are thorough
2~8min is stood after the fusing of bottom, melt temperature is then reduced to 1220~1380 DEG C and places 2~5min；Then by alloy
Melt is warming up to 1500 DEG C or more 2~5min of standing again, and then reduce electric current reduces melt temperature to 1150~1280 again
DEG C, and cast in common punching block and cooled down.Then microstructure observation (such as Fig. 1 is carried out to corresponding composite material
It is shown).
Embodiment 1
According to invention Cu-base composites composition design value, the raw material such as high-purity Cu and Fe-C intermediate alloys are cut first
It is placed in vacuum medium frequency induction furnace, melting and casting is carried out to it, specific melt casting process is：First burner hearth take out true
Sky closes vacuum pump when burner hearth vacuum degree is reduced to below 4Pa, while is filled with high-purity Ar gas and treats that burner hearth vacuum degree reaches
Stop inflation during more than 0.02MPa, start to heat up step by step when continuing to be evacuated down to below 4Pa, be warming up to 400~500 DEG C first
More than Shi Baowen 10min, then proceed to be warming up to 1500 DEG C or more and keep the temperature, and treat that the raw material such as Fe-C intermediate alloys and high-purity Cu are thorough
2~8min is stood after the fusing of bottom, melt temperature is then reduced to 1220~1380 DEG C and places 2~5min；Then by alloy
Melt is warming up to 1500 DEG C or more 2~5min of standing again, and then reduce electric current reduces melt temperature to 1150~1280 again
DEG C, and cast in the water cooled copper mould of logical recirculated water, cooling velocity is controlled 1.1 × 102DEG C/s~8.8 × 104DEG C/s models
In enclosing.Then microstructure observation (as shown in Figure 2) and performance measurement (as shown in table 2) are carried out to corresponding composite material.
Comparative example 2
Common cold-rolling deformation is carried out to advanced composite material (ACM) prepared by embodiment 1 and induces Fe-C phase martensite treatment process
For mode of texturing：Symmetric rolling, deformation temperature：10-35 DEG C, deflection 70~90%, passage dependent variable is 5%~20%.Most
Structure observation (as shown in Figure 3) and performance measurement are carried out (such as 2 institute of table to the Cu-base composites that Fe-C martensitic traoformations occur afterwards
Show).
Embodiment 2
The multiple deep cooling of advanced composite material (ACM) progress is prepared to embodiment 1 and rolls cycle induction Fe-C martensitic traoformation treatment process
For：Sample is placed into more than 30min in liquid nitrogen container first, then carries out ultralow warm deformation, deformation temperature：- 100~-190 DEG C,
Deflection：20%~29%, mode of texturing：Symmetric rolling, pass deformation are 10~20%；Then again by ultralow temperature milled sheet
Material is put into 2~9min of cooling, deformation temperature in liquid nitrogen container：- 100~-190 DEG C, deflection：20%~29%, mode of texturing：Together
Step rolling, pass deformation：10~20%；Then ultralow temperature rolled plate is put into 2~5min of cooling in liquid nitrogen container, deformation again
Temperature：- 100~-190 DEG C, deflection：20%~29%, mode of texturing：Symmetric rolling, pass deformation：10~20%；Most
Ultralow temperature rolled plate is put into 1~3min of cooling, deformation temperature in liquid nitrogen container again afterwards：- 100~-190 DEG C, deflection：15%
~25%, mode of texturing：Symmetric rolling, pass deformation：5~15%.Finally to the copper-based multiple of Fe-C martensitic traoformations occurs
Condensation material carries out structure observation (as shown in Figure 4) and performance measurement (as shown in table 2).
Embodiment 3
To advanced composite material (ACM) prepared by embodiment 1 certain high temperature, short time can be also carried out first to be heat-treated, then again into
The multiple deep cooling of row rolls the treatment process that cycle induces Fe-C martensitic traoformations.High temperature, short time heat treatment process is：With indifferent gas
It is carried out in the heat-treatment furnace of body protection, 800~920 DEG C of heat treatment temperature, time 2min~20min, then using water quenching method
It is cooled down.Then deep cooling is carried out again rolls cycle induction Fe-C martensitic traoformations treatment process (as described in Example 2).It is finally right
The Cu-base composites that Fe-C martensitic traoformations occur carry out structure observation (as shown in Figure 5) and performance measurement (as shown in table 2).
Comparative example 3
The composite material for inducing 2 common cold rolling of comparative example Fe-C transformations further carries out different temperatures heat treatment process
For：It is carried out in heat-treatment furnace with inert gas shielding, 100~400 DEG C, time 5min~120min of heat treatment temperature, so
It is cooled down afterwards using water quenching method.Micro-hardness measurement (such as table 3 finally is carried out to the composite material that heat treatment further regulates and controls
It is shown)
Embodiment 4
2 deep cooling of embodiment is rolled and induces the composite materials of Fe-C transformations and further carries out different temperatures heat treatment process and be：
It is carried out in heat-treatment furnace with inert gas shielding, then 100~400 DEG C of heat treatment temperature, time 5min~120min is adopted
It is cooled down with water quenching method.Micro-hardness measurement finally is carried out (such as 3 institute of table to the composite material that heat treatment further regulates and controls
Show)
Embodiment 5
3 deep cooling of embodiment is rolled and induces the composite materials of Fe-C transformations and further carries out different temperatures heat treatment process and be：
It is carried out in heat-treatment furnace with inert gas shielding, then 100~400 DEG C of heat treatment temperature, time 5min~120min is adopted
It is cooled down with water quenching method.Micro-hardness measurement finally is carried out (such as 3 institute of table to the composite material that heat treatment further regulates and controls
Show).
The mechanical property of 2 novel copper-based composite material different conditions of table
Influence of the heat treatment to hardness after 3 cold deformation of table induction Fe-C martensitic traoformations
Since the uniform distribution of forces of hardening constituent in metal-base composites directly determines the comprehensive performance of material, to protect
Card develops material with excellent comprehensive performance, it is necessary to the microscopic structure of founding state material be controlled well first.
As seen from Figure 1, comparative example 1 uses Fe-C phase uniform particles distributivity contained by composite material prepared by common casting method very
A degree of segregation occurs for difference, most of particle.But if quick solidified cast method is changed to (using embodiment 1
Preparation method), it can ensure that Fe-C phases particle is distributed shape in even dispersion in prepared novel copper-based composite material base body
State (as shown in Figure 2).Simultaneously because contained Fe-C phases particle is largely in the austenite of face-centred cubic structure in matrix,
There is good compatible deformation ability with Copper substrate, therefore, the composite material developed has extraordinary processing performance (such as table
Shown in 2), yield strength is only 171.5MPa, and elongation percentage is up to 35%, this elongation percentage is strong by ceramic particle far above tradition
The Cu-base composites of change.In order to enable the intensity of this high-ductility composite material is significantly promoted, it is necessary to its into
The subsequent strain inducing martensitic traoformation of row.Comparative example 2 is only with common cold-rolling deformation, although can equally induce in matrix
Martensite transfor mation occurs for Fe-C phases, but on the one hand possible transforming degree is limited, and another aspect Copper substrate crystal grain refinement is limited, most
Cause to use the microstructure of composite uniformity prepared by comparative example 2 not high (as shown in Figure 3), and composite material strength carries eventually
High-amplitude is also and little (as shown in table 2), and tensile strength is only 480.6MPa, and elongation percentage is also only 2.0%.In comparison, such as
Fruit induces Fe-C phase transition (embodiment 2) in matrix using deep cold-rolling deformation, and the structural homogenity for developing composite material is apparent
It improves (as shown in Figure 4), and its intensity and elongation percentage can obtain and further improve (as shown in table 2), tensile strength
Up to 568.1MPa, elongation percentage is also up to 5.0%.In addition, if certain height is carried out to quickly solidifying state composite material first
Temperature is heat-treated in short-term, is then carried out ultralow temperature depth cold-rolling deformation (as described in Example 3) again, can equally be ensured developed compound
Preferably (as shown in table 2), tensile strength is up to 538.6MPa, elongation percentage for material microstructure (as shown in Figure 5) and comprehensive performance
Also up to 4.0%.
In addition, in order to enable developed Cu-base composites comprehensive performance obtains further raising, it is necessary to cold change
The composite material that shape induces Fe-C phase transition makees further heat treatment, and reason is on the one hand can be with by being suitably heat-treated
So that a large amount of dislocation born of the same parents structural transformation is fine grain or nanometer crystal microstructure in Copper substrate, so as to improve the plasticity of composite material；Separately
On the one hand it is also possible that the Fe-C phase particles of a large amount of nanoscales are further precipitated in Copper substrate, so as to improve composite material
Intensity.If the similary composite material to common cold-rolling treatment carries out different temperatures heat treatment (as shown in comparative example 3), by table
3 as can be seen that compared with the hardness of cold rolling state composite material, its hardness is equal after the heat treatment of 100~400 DEG C of certain times
Generation changes to a certain degree, and in comparison, only by 250 DEG C and temperature below, treated that composite hardness slightly rises
Height, wherein the raising of 200 DEG C/60min treated hardness is maximum (up to 7HV), the composite material after other process is hard
Degree occurs to decline in various degree.And for rolling deformed composite material by deep cooling, although by subsequent heat treatment (strictly according to the facts
It applies 4 and implements 5), hardness also raises and reduces, but generally speaking, maximum hardness is above common cold after heat treatment
The hardness number that rolling compound material regulates and controls through Overheating Treatment, and the time for peak hardness occur be significantly shorter than common cold rolling composite wood
(as shown in table 3) of material.It can be seen that the advanced composite material (ACM) developed (or first carries out certain height using deep cold-rolling deformation
Temperature is heat-treated in short-term) and being aided with subsequent heat treatment regulation and control can enable composite material to show excellent comprehensive performance,
This performance strengthens Cu-base composites far above ceramic particle.
In conclusion it is of the invention by composition design, processing and optimization of Heat Treatment Process, in novel copper-based composite material
Size, structure, form and distribution of Fe-C phases etc. carry out Reasonable Regulation And Control after, can cause composite material simultaneously with
High intensity and excellent processing performance, so as to be provided more preferably to meet numerous high-technology fields the active demand of such material
It may.For this invention material and preparation method thereof due to simple for process, production cost is relatively low, in addition to numerous high-technology fields it
Outside, can also meet the needs of other product for civilian use fields process inexpensive Cu-base composites to high strength easy very well, be worth
Related Copper fabrication enterprise payes attention to the invention material and preparation method thereof, can obtain large-scale production as early as possible and push away
Wide application etc..
It although an embodiment of the present invention has been shown and described, for the ordinary skill in the art, can be with
Understanding without departing from the principles and spirit of the present invention can carry out these embodiments a variety of variations, modification, replace
And modification, the scope of the present invention is by appended claims and its equivalent limits.
Claims (3)
1. a kind of high strength easy processes Cu-base composites, it is characterised in that the chemical composition of the composite material and its quality percentage
It is than content：Fe 10.0wt%, C0.6wt%, P≤0.02wt%, Si≤0.01wt%, Ni≤0.01wt%, Zn≤
0.01wt%, Al≤0.01wt%, B≤0.01wt%, surplus Cu；
The preparation method of the composite material, includes the following steps：
Step 1: Cu-base composites vacuum melting；
Step 2: Cu-base composites quickly solidify；
Step 3: the Cu-base composites deformation induced martensitic traoformation process of ultralow temperature repeatedly；
Step 4: the heat treatment regulation and control of Cu-base composites nanometer crystal microstructure；
Wherein, step 1 and Cu-base composites vacuum melting described in step 2 and fast solidification technology are specially：First will
Raw material are placed in vaccum sensitive stove crucible and then burner hearth are vacuumized, and are closed when burner hearth vacuum degree is reduced to below 4Pa
Vacuum pump is closed, while is filled with high-purity Ar gas and stops inflation when burner hearth vacuum degree reaches more than 0.02MPa, continues to be evacuated down to
Start to heat up step by step during below 4Pa, keep the temperature more than 10min when being warming up to 400~500 DEG C first, then proceed to be warming up to 1500
DEG C or more keep the temperature, stand 2~8min after Fe-C intermediate alloys and high-purity Cu raw material thoroughly fusing, then drop melt temperature
As low as 1220~1380 DEG C and 2~5min is placed, alloy melt is then warming up to 1500 DEG C or more 2~5min of standing again,
Then reduce electric current reduces melt temperature to 1150~1280 DEG C, and cast in the water cooled copper mould of logical recirculated water again,
Cooling velocity is controlled 1.1 × 102DEG C/s~8.8 × 104DEG C/s in the range of；
The deformation induced martensitic traoformation process of ultralow temperature is specially Cu-base composites described in step 3 repeatedly：First by sample
Product place more than 30min in liquid nitrogen container, then carry out ultralow warm deformation, deformation temperature：- 100~-190 DEG C, deflection：20%
~29%, mode of texturing：Symmetric rolling, pass deformation are 10~20%；Then ultralow temperature rolled plate is put into liquid nitrogen again
2~9min of cooling, deformation temperature in tank：- 100~-190 DEG C, deflection：20%~29%, mode of texturing：Symmetric rolling, road
Secondary deflection：10~20%；Then ultralow temperature rolled plate is put into 2~5min of cooling, deformation temperature in liquid nitrogen container again：-100
~-190 DEG C, deflection：20%~29%, mode of texturing：Symmetric rolling, pass deformation：10~20%；It finally again will be ultralow
Warm-rolling panel is put into 1~3min of cooling, deformation temperature in liquid nitrogen container：- 100~-190 DEG C, deflection：15%~25%, become
Shape mode：Symmetric rolling, pass deformation：5~15%.
2. a kind of high strength easy processing Cu-base composites as described in claim 1, which is characterized in that step 3 becomes in deep cooling
Certain high temperature, short time heat treatment is carried out before shape first, then carries out repeatedly the deformation induced martensitic traoformation technique of ultralow temperature again
Processing；If the deformation induced martensitic traoformation process of ultralow temperature is certain using first carrying out repeatedly for the Cu-base composites
High temperature, short time is heat-treated, and then carries out ultralow temperature deformation process repeatedly again, high temperature, short time heat treatment process is specially：With lazy
It is carried out in the heat-treatment furnace of property gas shield, 800~920 DEG C of heat treatment temperature, time 2min~20min, then using water quenching
Mode is cooled down.
3. a kind of high strength easy processing Cu-base composites as described in claim 1, which is characterized in that copper-based described in step 4
The heat treatment of composite material nanometer crystalline substance tissue regulates and controls concrete technology：It is carried out in heat-treatment furnace with inert gas shielding, heat
Then 100~400 DEG C for the treatment of temperature, time 5min~120min are cooled down using water quenching method.
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| CN108220662B (en) * | 2017-12-06 | 2020-03-31 | 江西省科学院应用物理研究所 | Carbon microalloyed Cu-Fe system material and preparation method thereof |
| CN110863120B (en) * | 2019-11-01 | 2021-01-29 | 宁波金田铜业(集团)股份有限公司 | Copper alloy for lead frame and preparation method thereof |
| CN111910102B (en) * | 2020-07-14 | 2021-08-03 | 中南大学 | Copper-silver composite material wire and preparation method thereof |
| CN114293062A (en) * | 2021-12-09 | 2022-04-08 | 昆明冶金研究院有限公司北京分公司 | High-strength conductive anti-softening Cu-Ti alloy for elastic component and preparation method thereof |
Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN103952587A (en) * | 2014-04-30 | 2014-07-30 | 北京科技大学 | Complex phase copper alloy material and preparation method thereof |
| CN105088117A (en) * | 2015-09-17 | 2015-11-25 | 北京科技大学 | Treatment method for improving comprehensive performances of Cu-Fe-C complex phase copper alloy |
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| CN103952587A (en) * | 2014-04-30 | 2014-07-30 | 北京科技大学 | Complex phase copper alloy material and preparation method thereof |
| CN105088117A (en) * | 2015-09-17 | 2015-11-25 | 北京科技大学 | Treatment method for improving comprehensive performances of Cu-Fe-C complex phase copper alloy |
Non-Patent Citations (1)
| Title |
|---|
| The Martenstic Transformation of Iron Precipitation in a Copper Matrix;K.E.Easterling et al;《ACTA Metallurgica》;19670731;第15卷;第1133-1141页 * |
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